Amorphous alloy strip having a large thickness

Abstract

An iron base amorphous alloy strip having a sheet thickness of from 50 to 150 .mu.m and a sheet width of at least 20 mm. The strip is produced by a single-roll cooling process and has a fracture strain of 0.01 or more.

Description

BACKGROUND OF THE INVENTION

1. Field of the Invention

The present invention relates to amorphous alloy strips having a large thickness and a method for producing the same, more particularly to amorphous alloy strips having a large thickness produced by quenching and solidifying molten metal or alloy on a movable cooling substrate and a method for the same.

2. Description of the Related Art

It is well known to use a melt spin process to continuously produce amorphous strips from molten metal or alloy. In the melt spin process, molten metal is deposited onto a cooling substrate, e.g., the surface of annular chill roll, through a nozzle or nozzles. The molten metal is quenched and solidified by the cooling substrate, resulting in a continuous metal strip or wire.

In the melt spin process, the cooling rate is so high that, if the composition is suitably selected, an amorphous metal or alloy having substantially the same structure as the molten metal can be obtained. An amorphous metal or alloy has unique properties valuable for practical applications.

There are, however, some difficulties in obtaining wide strips. Important factors in the production of an amorphous metal or alloy are the shape of the nozzle, the relative arrangement of the nozzle and cooling substrate, the ejecting pressure of the molten metal through the nozzle, and the moving rate of the cooling substrate. To increase the width of the strip, one must meet severe conditions for each of the above.

A continuous casting method for a metallic amorphous strip and an apparatus for producing a wide strip are disclosed in Japanese Unexamined Patent Publication (Kokai) No. 53-53525. The method includes the steps of directing a slotted nozzle having a rectangular opening to a cooling substrate (roll or belt) with a gap of from about 0.03 to about 1 mm therebetween, advancing the cooling substrate at a speed to provide a peripheral velocity of from about 100 to about 2000 meters per minute, and ejecting molten metal to the chill surface of the cooling substrate through the slotted nozzle. The molten metal is quenched in contact with the chill surface at a rapid quenching rate and solidifies into a continuous amorphous metal strip. In this method, there is no limit on the width of the amorphous metal strip, in principle.

Restrictions on the cooling rate also make it difficult to obtain a thick strip. The problem of thickness of increasing the thickness of the strip has not been solved up until now. This limit on the thickness of the strip applies not only to amorphous metal requiring severe cooling conditions, but also to crystalline metal not requiring the same. The principal method adoptable to try to form a metal strip having a large thickness in the conventional continuous molten metal quenching process is to increase the advancing length of the puddle formed on the cooling substrate with respect to the advancing speed of the cooling substrate. In actual production of an amorphous metal strip, any one of the following means or combinations thereof may be considered to achieve this increase: The means are

1. To enlarge the width of the nozzle opening

2. To increase the forcing pressure

3. To increase the gap between the nozzle and the chill surface

4. To decrease the advancing speed of the cooling substrate

The present inventors experiments to produce an amorphous metal strip having a large thickness by using the above four means, but could not obtain good results. They found that there is a limit on thickness due to the type of metal or alloy and the material of the cooling substrate and that an unreasonable increase in thickness leads to an undesired shape and deterioration of the strip. Excessive molten metal, specifically, adheres to the nozzle and solidifies thereon. The solidified metal, which contacts the advancing chill surface, leads to nozzle breakage. Also, when a thick strip is produced by the above four means, the free surface of the metal strip is exposed to the atmosphere for a longer time, resulting in an undesired appearance, such as a rough surface, furrows, and coloring. Generation of such phenomena, in the case of an amorphous alloy, means also that crystal is formed on the surface layer, even if the crystal cannot be detected by X-ray diffraction. This reduces the ductility, the magnetic properties such as coercive force and core loss , and other properties of the amorphous alloy.

IEEE Trans., May 18 (1982) page 1385, discloses that if the strip thickness at which the coercive force begins to increase is defined as the critical strip thickness at which crystallization commences, the greatest critical strip thickness shown by an Fe-Si-B system alloy is 42 .mu.m of Fe.sub.76 -B.sub.10 -Si.sub.10. According to investigations by the present inventors, with Fe.sub.80.5 Si.sub.6.5 B.sub.12 C.sub.1 of a width of 25 mm, the critical strip thickness is 32 .mu.m. Further U.S. Pat. No. 4,331,739 discloses F.sub.40 Ni.sub.40 P.sub.14 B.sub.6 of a width of 5 cm, a thickness of 0.05 mm (50 .mu.m), and isotropic tensile properties.

Recently, an Fe base alloy strip having a width of 25.4 mm and a thickness of 82 .mu.m was reported (Journal of Applied Physics vol. 5, No. 6 (1984) P. 1787). According to the report, however, this alloy strip, of Fe.sub.80 B.sub.14.5 Si.sub.3.5 C.sub.2 showed the existence of 5% or less crystals under an X-ray diffraction test. As a consequence, the alloy strip as cast shows considerable brittleness. The fracture strain by bending stress of an 82 .mu.m thick Fe.sub.80 B.sub.14.5 Si.sub.3.5 C.sub.2 alloy is 0.006. The fracture strain .epsilon..sub.f is usually represented by the equation .epsilon..sub.f =t/(2r-t), wherein t is the strip thickness and r is the bending radius.

The more amorphous the alloy, the greater the fracture strain. A substantially amorphous alloy has a crystallization ratio of 1% or less as cast. The crystallization ratio is defined as follows:

Fc=(I-Io)/Ic wherein I is the diffraction intensity on a specified crystal face for example (110) face of a sample of a strip as cast, Io is the diffraction intensity on the same crystal face of a standard amorphous sample, and Ic is the diffraction intensity on the same crystal face upon complete crystallization.

SUMMARY OF THE INVENTION

The main object of the invention is to provide an Fe base alloy strip having a large sheet thickness and width.

Another object of the present invention is to provide an Fe base alloy strip having a large sheet thickness and width and having improved mechanical properties, particularly, bending fracture strain.

A further object of the present invention is to provide a method for producing an amorphous metal strip having a large sheet thickness and width and having improved properties.

According to the present invention, there is provided an Fe base amorphous alloy strip having a sheet thickness of from 50 to 150 .mu.m and a sheet width of at least 20 mm. The strip is produced by depositing molten metal onto the surface of a moving annular chill body in what is called a "Single-roll cooling process". This strip preferably has a surface roughness of the free surface and the constrained surface to the roll below 0.5 mm when measured by Japan Industrial Standard (JIS)-B0601. It also preferably has a fracture strain .epsilon..sub.f of 0.01 or more. In the present invention, "free surface" is defined as the strip surface which is not directly contacted with the chill surface of the roll during the production of amorphous strips. On the other hand, "constrained surfact to the roll" is defined as the strip surface which is in direct contact with the chill surface of the roll.

There is further provided a method for producing an amorphous metal strip by jetting a molten metal onto a chill surface of a rotating annular chill body for quenching, including the steps of drawing out a first molten metal on the moving chill surface through a first molten metal puddle portion to make a first strip; drawing out a second molten metal over the first strip as in a not completely solidified state of through a second molten metal puddle portion so as to make a second strip, the first strip being brought into strong contacted with the moving chill surface due to the pressure generated by the second puddle portion; and drawing out subsequent molten metals through further portions so as to make subsequent strips until the required sheet thickness is obtained. Tha resultant strip is a monolithic state strip.

BRIEF DESCRIPTION OF THE DRAWINGS

FIG. 1 is a graph illustrating the relationship between strip thickness and fracture strain in amorphous alloy strips according to the present invention and that of conventional alloy strips;

FIGS. 2 and 3 are graphs illustrating the relationships between strip thicknesses and heat of crystallization and between strip thicknesses and magnetic flux density;

FIG. 4 is a view explaining a method according to the present invention;

FIGS. 5 and 6 are views explaining nozzles used in a method according to the present invention;

FIG. 7 is a view illustrating a method for producing a strip according to the present invention;

FIG. 8 is a view of a bottom surface of a nozzle with nozzle openings used in the present invention;

FIGS. 9A and 9B are views illustrating the surface roughness of a free surface and constrained surface of an amorphous alloy strip according to the present invention;

FIGS. 9C and 9D are views illustrating the surface roughness of a free surface and constrained surface of comparative alloy strips;

FIGS. 10A and 10B are scanning electron micrographs illustrating a magnetic domain structure of a free surface of an amorphous alloy strip as cast according to the present invention and a conventional alloy strip;

FIGS. 11A and 11B are scanning electron micrographs illustrating a magnetic domain structure of a free surface, after annealing, of an amorphous alloy strip according to the present invention and a conventional alloy strip; and

FIGS. 12A and 12B are views illustrating the X-ray diffraction intensity of an amorphous strip having a thickness of 100 .mu.m according to the present invention and a conventional strip having a thickness of 30 .mu.m.

DESCRIPTION OF THE PREFERRED EMBODIMENTS

The Fe base amorphous alloy strip according to the present invention has a smoother constrained surface and free surface compared with a strip produced by a conventional process. As shown in Table 1, the centerline average surface roughness Ra at a cut off value of 0.8 mm measured by JIS B0601 is below 0.5 .mu.m for both the constrained surface and free surface. This is smaller, i.e., superior, compared with the 0.6 to 1.3 .mu.m of a conventional constrained surface and the 0.6 to 1.5 .mu.m of a conventional free surface.

With respect to the relationship between the surface roughness and magnetic properties, a smoother surface roughness means an improved coercive force, magnetic flux density and space factor. On the other hand, a thicker strip can be used for a large transformer as like a siliconsteel sheet and can be easily handled without deterioration of magnetic properties.

For example, since the amorphous alloy strip according to the present invention has a large thickness and smooth surface, the space factor is very high. The space factor of a conventional amorphous alloy strip having thinner thickness ranges from 75% to 85%, while, the space factor of an amorphous alloy strip according to the present invention ranges from 85% to 95%. Use of a material having a high space factor for, e.g., a magnetic core enables realization of a smaller core. Thus, a material having a high space factor is advantageous in practical use.

Even though the amorphous alloy strip of the present invention has a large thickness, no deterioration of its properties occur. The alloy strip remains substantially amorphous therethrough and so maintains its specific amorphous properties. For example, while a magnetic flux density at 50 Hz and 1 Oe of 1.53 tesla can be obtained in a conventional amorphous alloy strip of Fe.sub.80.5 Si.sub.6.5 B.sub.12 C.sub.1 (at %) having a thickness of 25 .mu.m and a width of 25 mm, the same magnetic flux density can be obtained in an amorphous alloy strip of Fe.sub.80.5 Si.sub.6.5 B.sub.12 C.sub.1 having a thickness of 65 .mu.m and a width of 25 mm according to the present invention. It is clear that no deterioration in magnetic flux density occurs.

The Fe base amorphous alloy strip by which the second object can be obtained is at least 50 .mu.m thick, at least 20 mm wide, and has a bending fracture strain (.epsilon..sub.f) of 0.01 or more, generally 0.15 or more, as mentioned above. On the other hand, the bending fracture strain .epsilon..sub.f in a conventional strip having the same thickness is below 0.01. Thus, the strip of the present invention has a 50% larger fracture strain than a conventional strip.

The reason why the strip of the present invention has improved mechanical properties will be hereinafter explained.

It is well known that the properties of an amorphous alloy strip depend on the sheet thickness. The sheet thickness of the strip will change the properties through thermal hysteresis. The decrease of the fracture strain which arises with an increase of the sheet thickness derives from the slower cooling rate of the strip during and after solidification. The slower cooling rate occurs as the sheet thickness of the strip become larger. Namely, when the thickness of the strip become larger, the amorphous structure of the strip is relaxed so that the structure of the strip becomes crystal, whereby the strip becomes brittle.

From this point of view, the strips of the present invention are produced so that the cooling rate is not decreased. In the present invention, although the sheet thickness of the strip is enlarged, the cooling rate during and after solidification is substantially the same phenomena as in the case of conventional strips having a sheet thickness of 30 .mu.m. Therefore, the time during which the strips of the present invention are relaxed becomes short, with the result that they have improved mechanical properties, particularly, a large bending fracture strain.

FIG. 1 is a graph illustrating the relationship between sheet thicknesses and fracture strain in amorphous alloy strips according to the present invention and that of conventional alloy strips. The amorphous alloy strips used consist of Fe.sub.80.5 Si.sub.6.5 B.sub.12 C.sub.1.

As shown in FIG. 1, when the sheet thickness of conventional strips exceeds 45 .mu.m, the fracture strain .epsilon..sub.f rapidly declines. When the sheet thickness is 50 .mu.m, the fracture strain is about 0.01. However, in the strips of the present invention, when the sheet thickness of the strips is 55 .mu.m, the fracture strain is 1. Namely, even if the strips of the present invention are bent at an angle of 180.degree., they will not fracture. In the case of a sheet thickness of 65 .mu.m, 180.degree. bending is impossible, but a fracture strain of 0.03 is obtained. In the case of a sheet thickness of 75 .mu.m, the fracture strain declines to 0.02. However, even in the case of a sheet thickness of 110 .mu.m, the fracture strain is above 0.01.

FIGS. 2 and 3 are graphs illustrating the relationships between strip thicknesses and heat of crystallization and between strip thicknesses and magnetic flux density.

As shown in FIG. 2, in an amorphous alloy strip of the present invention consisting of Fe.sub.80.5 Si.sub.6.5 B.sub.12 C.sub.1, the heat of crystallization .DELTA.H (J/g) is constant in cases of sheet thicknesses ranging from 20 .mu.m to 70 .mu.m. When the sheet thickness exceeds 70 .mu.m, the heat of crystallization is rapidly lowered. On the other hand, as shown in FIG. 2 (not shown) in the above-mentioned Journal of Applied Physics, the heat of crystallization is rapidly lowered at a sheet thickness of about 17 .mu.m. This means that the amorphous substance ratio of the strip of the present invention is higher than that of a conventional strip in a wide range of sheet thicknesses.

Further, as shown in FIG. 3, in a strip of the present invention having a sheet thickness below about 70 .mu.m, the core loss W.sub.13/50 (W/kg) is larger than that of a conventional strip of about 20 to 30 .mu.m. However the magnetic properties, for example, the magnetic flux density, in a strip of the present invention is substantially the same as in a conventional strip. We core loss increases due to the increase of the domain width, not to occurrence of crystals.

The amorphous alloy strip of the present invention includes Fe as a main component and includes one or more of boron, silicon, carbon, phosphorus, and the like as a metalloid. In accordance with the properties required, part of the iron may be substituted by another metal. For example, if a magnetic property is required, half the iron may be replaced with cobalt and/or nickel. In turn, in order to improve the magnetic property, one or more of molybdenum, niobium, manganese, and tin may be added. In order to improve corrosion resistance, one or more of molybdenum, chromium, titanium, zirconium, vanadium, hafnium, tantalum, and tungsten may be added. In order to improve mechanical properties, manganese, aluminum, copper, tin, or the like may be added. The content of iron may range from 40% to 82% (at %), boron from 8% to 17%, silicon from 1% to 15%, carbon below 3%, and residual elements below 10% in total. Above ranges of respective composition are selected in accordance with use.

With the amorphous alloy strips of the present invention are used as a core material, the strips are preferably composed of Fe.sub.a B.sub.b Si.sub.c C.sub.d. The ranges of a, b, c, and d are respectively 77 to 82, 8 to 15, 4 to 15, and 0 to 3.

The amorphous alloy strips according to the present invention are advantageously used for transformers, spring materials, corrosion resistant materials, sensors, structural materials, and the like.

A method for producing an amorphous alloy strip according to the present invention will now be explained in detail with reference to the drawings.

FIG. 4 is a view explaining the method according to the present invention, FIGS. 5 and 6 are views explaining nozzles used in the method, and FIG. 7 is another view illustrating the method according to the present invention.

As shown in FIGS. 4 and 5, a metal substance in usually melted by using a crucible 2. After that, molten metal 6 is flowed out on a cooling substrate 1, which moves in the direction of the arrow, through openings 4a and 4b of a nozzle 3.

As shown in FIG. 7, a puddle 5b composed of molten metal 6 flowed out through the second opening 4b is formed on an incompletely solidified strip 7a drawn out from a puddle 5a flowed out through the first opening 4a and formed on the cooling substrate 1. The strip 7b made of the puddle 5b is moved to the strip 7a. Since the strip 7a has sufficient cooling ability, the strip 7b is rapidly cooled together with the strip 7a, whereupon a monolithic sheet formed by the strips 7b and 7a is obtained.

As a result, strips having a large thickness can be continuously produced.

According to the present invention, the flowing out of the molten metal on the chill surface is preferably carried out under a pressurized atmosphere of, for example, 0.5 to 2 kg/cm.sup.2 larger pressure than ambient pressure anbient pressure. This pressure increases the contact force of the molten metal with the chill surface.

In the present method, at the stage of commencement of the solidification of metal, the molten metal contacts with the cooling substrate with a thermal effect. The cooling rate of the strip in the range of temperature most important for the properties of the strip is remarkably increased, enabling formation of a strip having twice or more the sheet thickness of strips produced by the conventional method.

According to the present invention, when, for example, multiple openings of nozzles are used, the opportunities for oxidation of the free surface of the strips and crystallization of the strips are considerably decreased. Thus, an amorphous alloy strip having a large sheet thickness according to the present invention does not suffer from deterioration of properties or undesired shape.

In the present invention, it is preferable that the atmosphere around the puddle be inert gas such as helium.

The gap between one puddle and a subsequent puddle may be selected so that when the strip portion formed via the one puddle contacts the strip portion formed via the subsequent puddle the former has not yet completely solidified. The most suitable gap is usually 4 mm or less. The width direction of the opening of the nozzle is oriented in parallel to the moving direction of the cooling substrate.

The size of the opening and the gap between openings may be selected as follows.

______________________________________Length (1) of opening: Substantially the same as the width of stripsWidth (w) of opening: Maximum 0.8 mm Minimum about 0.2 mmDistance (d) between openings: determined in accordance with shape and size of the opening and required sheet thickness; usually 0.5 to 4 mm______________________________________

To increase the sheet thickness of the strip, a plurality of openings having a small width may be used while keeping the gap between the openings small.

The present inventors have found that there is a certain range of sheet thickness in which strips having improved shapes and properties can be formed by a certain number of openings. For strips consisting of iron and metalloid, the range is 15 to 45 .mu.m for a single opening of a width of 0.4 mm; 30 to 60 .mu.m for two openings; and 40 to 70 .mu.m for three openings. These sheet thicknesses can be further increased by increasing the ejecting pressure during the casting.

Using this method, therefore, there should be no limit as to the sheet thickness in principle. However, there is an actual limit on the sheet thickness of the strips produced by the present invention due to the thermal conductivity and critical cooling rate of amorphous material. Still, the upper limit of the sheet thickness is remarkably raised as compared to the conventional method.

EXAMPLE 1

Alloys consisting of compositions described in Table 1 were cast in an amorphous alloy strip having a width of 25 mm by using a single roll made of copper and using three-slotted nozzles (w: 0.4 mm, l: 25 mm, d: 1 mm) as shown in FIG. 8. The production controls were an ejecting pressure of molten metal of 0.20 to 0.35 kg/cm.sup.2, a roll speed of 20 to 28 m/sec, and a gap between the nozzle and roll of 0.15 to 0.25 mm.

The sheet thickness, surface roughness, and space factor of the obtained amorphous alloy strips of the various compositions are shown in Table 1. Also shown are the typical levels of conventional strips produced by using a single roll. As shown in Table 1, in the strips of the present invention, the sheet thickness is large, the surface roughness small, and the space factor high compared to conventional strips.

FIGS. 9A and 9B are views illustrating the surface roughness of a free surface and a constrained surface of an amorphous alloy strip according to the present invention. FIGS. 9C and 9D are views illustrating the surface roughness of a free surface and a constrained surface of comparative alloy strips. The amorphous alloy strip of the present invention has a sheet thickness of 62 .mu.m, while the comparative alloy strip has a sheet thickness of 40 .mu.m.

FIGS. 10A and 10B are scanning electron micrographs illustrating the magnetic domain structure of a free surface of amorphous alloy strip No. 1 in Table 1 according to the present invention and a conventional alloy strip. The conventional alloy strip has a complex maze pattern of a magnetic domain structure, while the alloy strip of the present invention has, as cast, 180.degree. magnetic domains oriented in the same direction.

FIGS. 11A and 11B are scanning electron micrographs illustrating the magnetic domain structure of a free surface, after annealing, of an amorphous alloy strip according to the present invention and a conventional alloy strip. The amorphous alloy strip according to the present invention shown in FIG. 11A has a magnetic domain of a larger width than in the conventional alloy strip shown in FIG. 11B.

EXAMPLE 2

Alloys consisting of compositions described in Table 2 were cast into amorphous alloy strips having a width of 25 mm by using the same single roll, nozzle, 15 and production conditions as explained in Example 1.

The sheet thickness, surface roughness, and space factor of the obtained amorphous alloy strips of the various compositions are shown in Table 2.

As explained in Example 1, the alloy strips according to the present invention have improved properties.

TABLE 1__________________________________________________________________________ Surface roughness Sheet Ra (.mu.m) Space thickness Constrained Free factor B.sub.1 No. Composition (at %) .mu.m surface surface (%) (T)__________________________________________________________________________Strips of 1 Fe.sub.80.5 B.sub.12 Si.sub.7.5 62 0.41 0.44 90 1.52the present 2 Fe.sub.80.5 B.sub.12 Si.sub.6.5 C.sub.1 65 0.38 0.41 91 1.53invention 3 Fe.sub.78 B.sub.10 Si.sub.12 60 0.38 0.40 88 1.49 4 Fe.sub.78 B.sub.10 Si.sub.10 C.sub.2 62 0.29 0.38 90 1.50 5 Fe.sub.70.5 B.sub.12 Si.sub.7.5 Co.sub.10 65 0.38 0.40 91 1.61 6 Fe.sub.70.5 B.sub.12 Si.sub.7.5 Ni.sub.10 68 0.35 0.38 92 1.40 7 Fe.sub.75.5 B.sub.12 Si.sub.7.5 Mo.sub.5 71 0.40 0.46 92 0.97 8 Fe.sub.75.5 B.sub.12 Si.sub.7.5 Cr.sub.5 69 0.37 0.42 88 1.03 9 Fe.sub.75.5 B.sub.12 Si.sub.7.5 Nb.sub.5 70 0.30 0.39 90 1.05 10 Fe.sub.65.5 B.sub.12 Si.sub.7.5 Co.sub.10 Mo.sub.5 72 0.39 0.37 93 1.05 11 Fe.sub.65.5 B.sub.12 Si.sub.7.5 Ni.sub.10 Mo.sub.5 70 0.33 0.37 92 0.93 12 Fe.sub.65.5 B.sub.12 Si.sub.7.5 Ni.sub.10 Cr.sub.5 66 0.25 0.32 90 0.90 13 Fe.sub.65.5 B.sub.12 Si.sub.7.5 Co.sub.10 Cr.sub.5 57 0.36 0.40 90 1.03 14 Fe.sub.60.5 B.sub.12 Si.sub.7.5 Ni.sub.5 Co.sub.10 Cr.sub.5 55 0.38 0.46 89 1.01Comparative 15 Fe.sub.80.5 B.sub.12 Si.sub.7.5 36 0.81 0.60 84 1.52strips 16 Fe.sub.80.5 B.sub.12 Si.sub.6.5 C.sub.1 40 0.75 0.93 83 1.53 17 Fe.sub.78 B.sub.10 Si.sub.12 23 0.64 0.63 83 1.48__________________________________________________________________________ B.sub.1 : Magnetic flux density in 50 Hz, 1 Oe Ra: Cutoff value 0.8 mm, measured length 8 mm Space factor: About 700 g strip was wound up on a reel having outer diameter of 40 mm. ##STR1## - Wherein the calculated weight is (R.sup.2 - r.sup.2) .pi. R: outer diameter of ring r: inner diameter of ring w: width .rho.: specific weight TABLE 2__________________________________________________________________________ Surface roughness Sheet Ra (.mu.m) Space thickness Constrained Free factor No. Composition (at %) .mu.m surface surface (%)__________________________________________________________________________Strips of 1 Fe.sub.80 P.sub.13 C.sub.7 65 0.39 0.41 91the present 2 Fe.sub.72 P.sub.13 C.sub.7 Cr.sub.8 62 0.45 0.44 90invention 3 Fe.sub.70 P.sub.10 C.sub.10 Cr.sub.10 59 0.38 0.38 94 4 Fe.sub.50 P.sub.13 B.sub.7 Ni.sub.30 67 0.48 0.42 90 5 Fe.sub.50 P.sub.13 B.sub.7 Co.sub.30 70 0.32 0.37 93 6 Fe.sub.76 P.sub.13 C.sub.3 Si.sub.4 Cr.sub.4 62 0.41 0.39 91Comparative 7 Fe.sub.80 P.sub.13 C.sub.7 28 0.68 0.61 84strips 8 Fe.sub.80 P.sub.13 C.sub.7 33 0.78 0.87 82 9 Fe.sub.80 P.sub.13 C.sub.7 41 0.81 0.90 81__________________________________________________________________________

EXAMPLE 3

An alloy consisting of Fe.sub.80.5 Si.sub.6.5 B.sub.12 C.sub.1 (at %) was cast into an amorphous alloy strip by using substantially the same production conditions explained in Example 1.

The sheet thickness, bending fracture strain .epsilon..sub.f, and other properties are shown in Table 3. Also shown are the properties of Co conventional alloy strip produced by using a single-slotted nozzle (d: 0.7 mm, 1: 25 mm).

TABLE 3______________________________________ Sheet Space thickness factor (.mu.m) .epsilon..sub.f Ra (.mu.m) (%)______________________________________Strip of 65 0.03 Roll Free 91the present surface surfaceinvention 0.35 0.40Comparative 50 0.0065 0.80 1.05 83strip______________________________________

EXAMPLE 4

An alloy consisting of Fe.sub.80.5 Si.sub.6.5 B.sub.12 C.sub.1 was cast into an amorphous alloy strip by using a single roll and a four-slotted nozzle (w: 0.4 mm, 1: 25 mm, d: 1 mm) and an ejecting pressure of molten metal of 0.3 kg/cm.sup.2. During the casting, the roll speed was changed from 25 m/sec to 18 m/sec. At the time the roll speed was changed, the free surface of the strip was pressurized by helium gas. A comparative strip was also cast by using the same nozzle as explained in Example 3. The roll speed was also changed as mentioned above.

The obtained properties are shown in Table 4.

TABLE 4______________________________________ Sheet Space thickness factor (.mu.m) .epsilon..sub.f Ra (.mu.m) (%)______________________________________Strip of 75 0.02 Roll Free 93according to surface surfacethe present 0.32 0.35inventionComparative 56 0.005 0.82 1.13 85strip______________________________________

EXAMPLE 5

An alloy consisting of Fe.sub.80.5 Si.sub.6.5 B.sub.12 C.sub.1 was also cast into an amorphous alloy strip by using the two-slotted nozzle as shown in FIG. 5 (l: 25 mm, w: 0.4 mm, d: 1 mm) and a single roll made of copper. The production controls were an ejecting pressure of molten metal of 0.22 kg/cm.sup.2, a roll speed of 25 m/sec, and a gap between the nozzle and roll of 0.15 mm. The sheet thicknesses of the obtained strips were an average 45 .mu.m. Further crystallization was not found in the strips by X-ray diffractometry. The magnetic properties of the strip according to the present invention are substantially the same as those of a conventional strip produced by using a single nozzle, as shown in Table 5.

TABLE 5______________________________________Sheet Magnetic fluxthickness Core loss W.sub.1.3/50 density B.sub.1(.mu.m) (Watt/kg) (Tesla)______________________________________35 0.23 1.3226 0.10 1.5145 0.11 1.52______________________________________ (Heat treatment: 380.degree. C. .times. 1 hr)

EXAMPLE 6

An alloy consisting of Fe.sub.80.5 Si.sub.6.5 B.sub.12 C.sub.1 was cast into an amorphous alloy strip by using a three-slotted nozzle as shown in FIG. 6 (l: 25 mm, w: 0.4 mm, d.sub.1 =d.sub.2 : 1.0 mm) and a single roll. The production conditions were the same as explained in Example 5. The sheet thickness of the obtained strips was an average 60 .mu.m. Further, non-crystallization was found in the strips. The magnetic properties, shown in Table 6, are substantially the same as the strips produced by the conventional method.

TABLE 6______________________________________Sheet Magnetic fluxthickness Core loss W.sub.1.3/50 density B.sub.1(.mu.m) (Watt/kg) (Tesla)______________________________________62 0.125 1.53______________________________________

EXAMPLE 7

An alloy consisting of 6.5 wt% silicon steel was cast into an amorphous alloy strip by using a three-slotted nozzle as shown in FIG. 6 (l: 25 mm, w: 0.4 mm, d.sub.1 =d.sub.2 : 1.5 mm) and a single roll made of iron. The production conditions were an ejecting pressure of molten metal of 0.22 kg/cm.sup.2, a roll speed of 22 m/sec, and a gap between the nozzle and the roll of 0.2 mm. The sheet thickness and the crystal grain size of the obtained strips were an average 63 .mu.m and 10 .mu.m, respectively. The surface property and the shape of the strip were remarkably improved.

EXAMPLE 8

An amorphous stainless steel strip consisting of C.sub.0.06 Si.sub.0.6 Mn.sub.0.5 P.sub.0.025 S.sub.0.005 (wt%) was produced by using a single roll made of iron and the nozzle in Example 7. The production conditions were the same as explained in Example 7.

The sheet thickness and the crystal grain size were an average 58 .mu.m and 5 .mu.m, respectively. The properties were improved.

EXAMPLE 9

An amorphous alloy strip consisting of Fe.sub.80 Mo.sub.4 B.sub.12 C.sub.4 (at %) was produced by using a four-slotted nozzle (l: 25 mm, w: 0.4 mm, d: 1.0 mm). The production conditions were a first ejecting pressure of molten metal of 0.08 kg/cm.sup.2, a second ejecting pressure of 0.22 kg/cm.sup.2, a roll speed of 12 m/sec, and a gap between the nozzle and the roll of 0.15 to 0.18 mm.

The sheet thickness of the obtained strip was an average 100 .mu.m. The strips were found to be amorphous by x-ray diffractometry.

FIGS. 12A and 13 are views illustrating the X-ray diffraction intensity of an amorphous strip having a thickness of 100 .mu.m according to the present invention and a conventional strip having a thickness of 30 .mu.m.

It can be see from FIGS. 12 and 13 that the X-ray diffraction intensity of the strip of the present invention is substantially the same as that of a conventional strip.

EXAMPLE 10

An amorphous alloy strip consisting of Fe.sub.80 Mo.sub.4 B.sub.12 C.sub.4 (at %) was produced by using a four-slotted nozzle (1: 25 mm, w: 0.4 mm, d: 1.0 mm). The production conditions were a first ejecting pressure of molten metal of 0.08 kg/cm.sup.2, a second ejecting pressure of 0.28 kg/cm.sup.2, a roll speed of 12 m/sec, and a gap between the nozzle and the roll of 0.15 to 0.18 mm.

The sheet thickness of the obtained strip was an average 120 .mu.m. The strips were found to be amorphous by X-ray diffractometry. The X-ray diffraction intensity was substantially the same as that of the Example 9.

Claims

1. A method of producing a thick amorphous alloy strip by ejecting a molten metal onto a surface of a moving cooling substrate for quenching, comprising the steps of:

providing said moving cooling substrate by using a single-roll cooling process;

ejecting under pressure a first molten metal through a first nozzle opening onto the moving cooling substrate to form a first molten metal puddle portion;

drawing out first molten metal from the first molten metal puddle portion to form a strip, by moving the moving cooling substrate in a predetermined direction;

ejecting under pressure a second molten metal having the same composition as the first molten metal through a second nozzle opening spaced 0.5 to 4 mm from the first nozzle opening along the moving direction of the cooling substrate and formed in parallel with the first nozzle opening, said second molten metal being ejected on the surface of the strip, the strip being incompletely solidified, with said second molten metal forming a second molten metal puddle portion, wherein the second molten metal of the second molten metal puddle portion mixes with non-solidified metal of the incompletely solidified strip, the non-solidified metal of the incompletely solidified strip being located at a top portion of said strip facing said second nozzle opening and forming the surface of the strip onto which the second molten metal is ejected;

drawing out second molten metal from the second molten metal puddle portion to form an initial monolithic strip composed of the second molten metal and the incompletely solidified strip, the strip being brought into firm contact with the surface of the moving cooling substrate due to said ejection under pressure thereby increasing cooling rate; and

thereby obtaining a monolithic metal strip having a thickness of at least 50 .mu.m and having a fracture strain of 0.01 or more upon complete solidification of said strip.

2. A method according to claim 1, wherein said drawing out of the molten metal is carried out in a pressurized atmosphere.

3. A method according to claim 1, wherein said drawing out of the molten metal is carried out by increasing an ejecting pressure thereof during the method.

4. A method according to claim 1, wherein the gap between said molten metal puddle portions is 4 mm or less.

5. A method according to claim 1, wherein said drawing out of the molten metal is carried out in a helium atmosphere.

6. A method of producing a thick amorphous alloy strip according to claim 25 further comprising:

ejecting under pressure at least one subsequent molten metal having the same composition as the first molten metal through at least one subsequent nozzle opening spaced 0.5 to 4 mm from the preceding nozzle opening, said subsequent molten metal being ejected on the surface of the initial monolithic strip, the initial monolithic strip being incompletely solidified and having non-solidified metal located at a top portion of said initial monolithic strip facing said subsequent nozzle opening and forming the surface of the initial monolithic strip onto which said subsequent molten metal is ejected, with said subsequent molten metal forming a subsequent molten metal puddle portion, wherein the subsequent molten metal of the subsequent molten metal puddle portion mixes with the non-solidified metal of the initial monolithic strip; forming a subsequent monolithic strip by drawing out subsequent molten metal from said subsequent molten metal puddle portion; thereby obtaining the monolithic metal strip having a thickness of at least 50 .mu.m and having a fracture strain of 0.01 or more upon complete solidification of said strip.